EP2687617B1 - High-purity ferritic stainless steel sheet with excellent corrosion resistance and anti-glare properties - Google Patents

High-purity ferritic stainless steel sheet with excellent corrosion resistance and anti-glare properties Download PDF

Info

Publication number
EP2687617B1
EP2687617B1 EP12756952.3A EP12756952A EP2687617B1 EP 2687617 B1 EP2687617 B1 EP 2687617B1 EP 12756952 A EP12756952 A EP 12756952A EP 2687617 B1 EP2687617 B1 EP 2687617B1
Authority
EP
European Patent Office
Prior art keywords
annealing
steel sheet
corrosion resistance
stainless steel
surface film
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Active
Application number
EP12756952.3A
Other languages
German (de)
English (en)
French (fr)
Other versions
EP2687617A1 (en
EP2687617A4 (en
Inventor
Masaharu Hatano
Hiroyuki Matsuyama
Akihito Yamagishi
Naoto HANSAKI
Eiichiro Ishimaru
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nippon Steel Stainless Steel Corp
Original Assignee
Nippon Steel and Sumikin Stainless Steel Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Nippon Steel and Sumikin Stainless Steel Corp filed Critical Nippon Steel and Sumikin Stainless Steel Corp
Publication of EP2687617A1 publication Critical patent/EP2687617A1/en
Publication of EP2687617A4 publication Critical patent/EP2687617A4/en
Application granted granted Critical
Publication of EP2687617B1 publication Critical patent/EP2687617B1/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0268—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment between cold rolling steps
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12861—Group VIII or IB metal-base component
    • Y10T428/12951—Fe-base component
    • Y10T428/12972—Containing 0.01-1.7% carbon [i.e., steel]
    • Y10T428/12979—Containing more than 10% nonferrous elements [e.g., high alloy, stainless]

Definitions

  • the present invention relates to an alloy-saving type dull finish high purity ferritic stainless steel sheet excellent in corrosion resistance and anti-glare property which is suitable for use for household electrical appliances or kitchen appliances and interior or external siding in building materials, and a production method thereof.
  • dull finish “dull finish rolling”, dull rolls, dull roll rolling, etc. shall mean deluster finish, deluster finish rolling, deluster rolls, deluster rolling, etc.
  • Ferritic stainless steel sheet is being used in a wide range of fields such as household electrical appliances or kitchen appliances and interior or external siding in building materials. In recent years, improvements in the art of refining have made much lower carbon and nitrogen contents and reduction of P, S, and other impurity elements possible. Ferritic stainless steel sheet which has been raised in corrosion resistance and workability by adding Nb, Ti, and other stabilizing elements (below, "high purity ferritic stainless steel sheet”) is being applied to a broad range of applications. This is because high purity ferritic stainless steel sheet is superior in terms of economy compared with austenitic stainless steel sheet which contains a large amount of Ni - an element whose price has remarkably lowered in recent years.
  • ferritic stainless steel sheet In recent years, in high purity ferritic stainless steel sheet excellent in corrosion resistance, demand has been rising for an anti-glare property as one facet of the surface quality of steel sheet not only in interior and exterior siding in building materials, but also in household electrical appliances and kitchen appliances. In general, ferritic stainless steel sheet is inferior compared to austenitic stainless steel sheet in anti-glare property. Austenitic stainless steel sheet relatively easily forms intergranular corrosion grooves by nitric hydrofluoric acid pickling. Due to the random reflection of light by the microrelief shapes, it is easy to obtain surface properties excellent in milky white color and low luster anti-glare property.
  • high purity ferritic stainless steel sheet contains large amounts of at least one of Cr and Mo so is high in alloying degree and has Nb, Ti, etc. added as stabilizing elements. Therefore, high purity ferritic stainless steel sheet is high in intergranular corrosion resistance and is not formed with intergranular corrosion grooves in annealing and pickling. This is disadvantageous for securing an anti-glare property.
  • PLT 1 discloses a method of production of dull finish stainless steel sheet excellent in anti-glare property, color tone uniformity, and corrosion resistance comprising annealing and pickling stainless cold rolled steel sheet in the atmosphere, then lightly rolling it by dull rolls and further annealing or bright annealing, then pickling it in the atmosphere.
  • PLT 2 discloses a method of production of dull finish stainless steel sheet comprising, during the pickling performed before and after dull finish rolling of the sheet, prescribing in detail the conditions of electrolytic pickling by a sulfuric acid aqueous solution and nitric acid aqueous solution and conditions of dipping in a nitric hydrofluoric acid aqueous solution.
  • PLT 1 and PLT 2 disclose examples of SUS304 and SUS444 of the Japan Industrial Standard (JIS standard), but do not disclose details of the chemical composition of the steel.
  • PLT 3 discloses ferritic stainless steel sheet which contains Cr: 16 to 35% and Mo: less than 6% and further contains one or more of Nb: 0.01 to 1%, Ti: 0.01 to 0.5%, V: 0.01 to 0.3%, Cu: 0.5% or less, and Al: 0.005 to 0.3%, in which ferritic stainless steel sheet, the conditions of electrolytic pickling in the nitric acid aqueous solution are defined and the color tone stability anti-glare property and corrosion resistance are improved, and a method of production of the same.
  • PLT 4 discloses ferritic stainless steel sheet which contains C ⁇ 0.02%, N ⁇ 0.020, Cr: 21.5 to 31%, Mo: 0.3 to 4%, Ti: 0.1 to 0.3%, and Nb: 0.15 to 0.5% and satisfies Cr+1.7Mo ⁇ 24%, in which ferritic stainless steel sheet, annealing is performed in an oxidizing atmosphere, the conditions of nitric hydrofluoric acid pickling after that are defined, and the corrosion resistance is improved, and a method of production of the same.
  • PLT 5 discloses high Cr-content bright annealed stainless steel sheet which has a chemical composition of which satisfies C ⁇ 0.020, Si ⁇ 1%, Mn ⁇ 1%, P ⁇ 0.040, Ni ⁇ 0.6%, Cr: 16 to 35%, Ti: 0.05 to (0.5-10 ⁇ N), Al: 0.005 to 0.3%, Mo ⁇ 0.6%, Nb ⁇ 1%, Cu ⁇ 0.50, and N ⁇ 0.02%, in which ferritic stainless steel sheet, details of the bright annealing conditions are defined and the surface of the steel sheet is formed with relief shapes with a 10-point average roughness Rz of 1 to 50 ⁇ m, whereby an anti-glare property is imparted and the surface quality of the steel sheet is improved, and a method of production of the same.
  • PLTs 3 to 5 disclose examples of ferritic stainless steel sheet which contain Cr: 22% or more and Mo. Therefore, the stainless steel sheets which are disclosed in PLTs 3 to 5 relate to high purity ferritic stainless steel sheet which contains large amounts of at least one of the above-mentioned Cr and Mo.
  • PLT 6 discloses ferritic stainless steel sheet which contains C ⁇ 0.030, Si ⁇ 0.3%, Mn ⁇ 1%, P ⁇ 0.080, S ⁇ 0.02%, Cr: 10 to 35%, N ⁇ 0.080, Nb: 0.05 to 2%, Ti: 0.05 to 2%, and Al: 0.08 to 0.8%, in which ferritic stainless steel sheet, a surface film which is formed by bright annealing contains Al: 15 at% or more and Nb: 6 at% or more and further Ti, a surface roughness is made an average roughness Ra of 0.3 ⁇ m to 0.95 ⁇ m to impart an anti-glare property, and the corrosion resistance and workability are improved.
  • the ferritic stainless steel sheet of PLT 6 defines the surface film which is formed by the bright annealing so as to improve the corrosion resistance without including large amounts of at least one of Cr and Mo.
  • the high purity ferritic stainless steel sheets which are proposed in PLTs 7 and 8 are high purity ferritic stainless steels which contain Cr: 13 to 22% and Sn: 0.001 to 1%, which reduce the C, N, Si, Mn, and P, have Al in 0.005 to 0.05% in range, and, in accordance with need, have stabilizing elements of at least one of Ti and Nb added.
  • conventional stainless steel sheet has been high alloy type high purity ferritic stainless steel sheet which contains Cr in a content of 22% or more and Mo so as to doubly provide corrosion resistance.
  • high purity ferritic stainless steel sheet which does not rely on addition giving a large amount of at least one Cr and Mo, which control the composition of the surface film, has also been disclosed, but it has been limited to the surface film which is formed by bright annealing. Further, high purity ferritic stainless steel to which a fine amount of Sn has been added from the viewpoint of resource-saving and economy has been disclosed, but the anti-glare property and corrosion resistance have not been studied.
  • an object of the present invention is to provide an alloy-saving type high purity ferritic stainless steel sheet which does not rely on high alloying by addition giving a large content of at least one of Cr and Mo, which is further not limited to a surface film formed by bright annealing, and which makes use of addition of Sn to doubly provide an anti-glare property and corrosion resistance.
  • the inventors worked to solve the above-mentioned problem by engaging in in-depth research on the effects of addition of Sn on the relationship of surface properties giving an anti-glare property and corrosion resistance in high purity ferritic stainless steel while focusing on the action and effect of a surface film which improves the corrosion resistance. As a result, they obtained the new discovery explained next.
  • the present invention was made based on the findings of the above (a) to (f) and relates to the following:
  • an alloy-saving type high purity ferritic stainless steel sheet not relying on high alloying by addition giving a large content of at least one of Cr and Mo and, further, not limited to a surface film which is formed by bright annealing and adding Sn to high purity ferritic stainless steel sheet to be able to doubly provide an anti-glare property and corrosion resistance.
  • Si is an element which is effective as a deoxidizing element and also has the action of raising the corrosion resistance of the present invention.
  • the lower limit is made 0.01%.
  • the upper limit is made 1%.
  • the content is made 0.1 to 0.6%. more preferably 0.15 to 0.5%.
  • Mn is an element which forms sulfides and interferes with the corrosion resistance, so the smaller the content, the better.
  • the upper limit is made 1.5%.
  • the lower limit is made 0.01%.
  • the content is made 0.05 to 0.5%.
  • the upper limit is made 0.05%.
  • the lower limit is made 0.005%.
  • the content is made 0.01 to 0.04%.
  • the upper limit is made 0.01%.
  • the lower limit is made 0.0001%.
  • the content is made 0.0002 to 0.002%.
  • Cr is a major element in the high purity ferritic stainless steel of the present invention. It is an element which is essential for improving the corrosion resistance which is targeted by the present invention by addition of Sn. To obtain the effect of improvement of the corrosion resistance of the present invention, the lower limit is made 13%. The upper limit is made 30% from the viewpoint of the manufacturability. However, from the economy compared with SUS304 or 22%Cr-1%Mo steel, preferably the content is made 14 to 22%. Considering the performance and the alloy cost, the content is more preferably 16 to 18%.
  • N in the same way as C, causes the corrosion resistance to degrade, so the smaller the content the better, therefore the upper limit is made 0.03%.
  • the lower limit is made 0.001%.
  • the content is made 0.005 to 0.015%.
  • Al is an element effective as a deoxidizing element and in addition is an element essential for improvement of the corrosion resistance which is targeted by the present invention.
  • the lower limit is made 0.005% to obtain the effect of improvement of the corrosion resistance superposed with the addition of Sn.
  • the upper limit is made 1% from the viewpoint of the manufacturability and the weldability and workability. However, from the performance and manufacturability compared with SUS304 and 22%Cr-1%Mo steel, the content is preferably 0.03 to 0.8%. More preferably, it is made 0.05 to 0.5%.
  • Sn is an element essential for securing the improvement in the corrosion resistance which is targeted by the present invention in surface properties giving an anti-glare property without relying on alloying by at least one of Cr and Mo or bright annealing for control of the surface film.
  • the lower limit is made 0.01%.
  • the upper limit is made 1% from the viewpoint of the manufacturability.
  • the content is preferably 0.1 to 0.6%. Considering the performance and alloy cost, the content is more preferably 0.2 to 0.5%.
  • Nb and Ti are elements which improve the corrosion resistance by the action of stabilizing elements which fix the C and N and are added in accordance with need.
  • the contents are made 0.03% or more where the effects are manifested.
  • excessive addition leads to a rise in the alloy cost and to a drop in the manufacturability accompanying the rise in the recrystallization temperature, so the upper limits are made 0.5%.
  • Nb and Ti are preferably made 0.05 to 0.5%. More preferably, the contents are made 0.1 to 0.3% in range.
  • Ni, Cu, Mo, V, Zr, and Co are elements which are effective for raising the corrosion resistance due to the synergistic effect with the Sn and are added in accordance with need.
  • Ni, Cu, and Mo, when added, are respectively made 0.1% or more where their effects are manifested.
  • V, Zr, and Co, when added, are made 0.01% or more where their advantageous effects are manifested.
  • excessive addition leads to a rise in the alloy cost or a drop in the manufacturability, so the upper limit is made 0.5%.
  • Mg forms Mg oxides in the molten steel together with the Al to act as a deoxidizer and also acts as a nuclei for precipitation of TiN.
  • TiN becomes the nuclei for solidification of the ferrite phase in the solidification process and promotes the precipitation of TiN so enables fine formation of a ferrite phase at the time of solidification.
  • the content is made 0.0001% where the effects are exhibited. However, if over 0.005%, the manufacturability deteriorates, so the upper limit is made 0.005%. Preferably, considering the manufacturability, the content is made 0.0003 to 0.002%.
  • B is an element which improves the hot workability and secondary workability. Addition to high purity ferritic stainless steel is effective. When added, the content is made 0.0003% or more for expressing these effects. However, excessive addition causes a drop in the elongation, so the upper limit is made 0.005%. Preferably, considering the material costs and workability, the content is made 0.0005 to 0.002%.
  • Ca is an element which improves the hot workability and the cleanliness of the steel and is added according to need.
  • the content is made 0.0003% or more where these effects are manifested.
  • the upper limit is made 0.005%.
  • the content is made 0.0003 to 0.0015%.
  • La, Y, Hf, and REM have the effects of improving the hot workability and the cleanliness of the steel and remarkably improving the corrosion resistance and the hot workability, so may be added in accordance with need.
  • the contents are respectively made 0.001% or more where these effects are manifested.
  • excessive addition leads to a rise in the alloy cost and a drop in the manufacturability, so the upper limits are respectively made 0.1%.
  • the content for one or more types is made 0.001 to 0.05%.
  • the surface roughness of the steel sheet is made an arithmetic average roughness Ra of 0.1 ⁇ m or more.
  • the arithmetic average roughness Ra is made 1.5 ⁇ m. Considering the advantageous effect and the manufacturability, in the claimed invention the arithmetic average roughness Ra is 0.2 to 1.0 ⁇ m. The preferable Ra is 0.5 to 0.9 ⁇ m.
  • the method of production for obtaining the above surface properties is not particularly defined, but to realize the above effects on an industrial production scale, it is preferable to produce the steel sheet through the following such production process and various conditions.
  • the claimed invention also relates to a method for producing a high purity ferritic stainless steel sheet excellent in corrosion resistance and anti-glare property as set forth in claim 1, wherein the claimed method is as defined in claim 2.
  • the extraction temperature after the heating in hot rolling of a cast slab is made 1100°C or more where scale easily forms by the chemical composition of the high purity ferritic stainless steel sheet of the present invention. This is because to secure excellent surface properties, it is effective to remove inclusions at the cast slab surface, which would otherwise cause scabs, by the formation of scale.
  • the target for the amount of formation of scale is a thickness of scale of 0.1 mm or more.
  • the hot rolling heating temperature is 1200°C or less to stabilize the TiCS.
  • the coiling temperature after hot rolling is made 700°C or less enabling the steel toughness to be secured and enabling internal oxides and internal oxidation which would invite a drop in surface properties to be suppressed. This is because if over 700°C, the precipitates including Ti and P would easily precipitate and would be liable to lead to a drop in the corrosion resistance. On the other hand, if making the coiling temperature after hot rolling less than 400°C, poured water after hot rolling is liable to invite shape defects in the hot rolled steel strip and induce surface defects at the time of uncoiling or sheet running. Considering the chemical composition of the high purity ferritic stainless steel sheet of the present invention and the improvement of the corrosion resistance which is targeted by the present invention, it is preferable that the coiling temperature after hot rolling be made 500 to 600°C.
  • the annealing temperature of the hot rolled sheet when annealing the hot rolled sheet is 850 to 1050°C if considering the drop in the surface properties and the pickling descalability.
  • the annealing of the hot rolled sheet is preferably performed at 900°C or more when adding, in addition to Sn and Cr, Nb and Ti and other stabilizing elements.
  • the sheet When annealing the hot rolled sheet, after annealing the hot rolled sheet, or, when omitting the annealing of the hot rolled sheet, after the hot rolling, the sheet is cold rolled once or cold rolled two times or more with process annealing in between.
  • the cold rolling is made the following process in order to obtain the anti-glare property and corrosion resistance of the present invention without impairing the productivity.
  • dull rolls are used for dull finish rolling.
  • dull roll rolling is performed using dull rolls which were treated by electrodischarge to give roll surfaces with an arithmetic average roughness Ra of 1 to 10 ⁇ m.
  • the productivity is inferior, but the dull finish may be given in the following way, which is however not part of the claimed invention. That is, normal cold rolling is performed, then annealing and pickling or bright annealing is performed, then the softened steel sheet is rolled by dull roll rolling to give it a dull finish. This is so as to reduce the variation in color tone in the dull finish rolling and facilitate transfer of the dull pattern.
  • the dull finish cold rolled steel sheet is improved in the corrosion resistance which is targeted by the present invention by next annealing and pickling it in an oxidizing atmosphere or bright annealing it.
  • the annealing temperature in the oxidizing atmosphere is 1000°C or less. This is so as to reduce the changes in the surface properties accompanying the formation of oxide scale.
  • the lower limit of the annealing temperature in an oxidizing atmosphere is made 800°C. This is so as to cause complete recrystallization by the chemical composition of the high purity ferritic stainless steel sheet of the present invention.
  • the pickling method is not particularly prescribed. It may be an ordinary method which is industrially used. For example, there is the method of dipping in an alkali salt bath, electrolytic pickling, then dipping in nitric hydrofluoric acid.
  • the electrolytic pickling may be neutral salt electrolysis, nitric acid electrolysis, etc.
  • the bright annealing temperature is made 800 to 1000°C in range.
  • hydrogen gas or a mixed gas of hydrogen and nitrogen is used for the atmospheric gas.
  • the dew point of the atmospheric gas is made -70 to -30°C in range. More preferably, hydrogen gas is made 80% or more and the dew point of the atmospheric gas is made -50°C or less.
  • Bright annealed steel sheet may be treated by nitric acid electrolysis in accordance with need in order to raise the concentration of Cr in the surface film.
  • the high purity ferritic stainless steel sheet of the present invention has a surface film.
  • the average concentration of Cr in the surface film has to be 1.1 times or more the concentration of Cr inside the steel sheet. This is because if the average concentration of Cr in the surface film is less than 1.1 times the concentration of Cr inside of the steel sheet, it is not possible to secure an anti-glare property while obtaining the desired corrosion resistance.
  • the concentration of Cr inside of the steel sheet means the amount of Cr which is contained in the steel sheet.
  • the surface film has to contain, in addition to Sn, and when the high purity ferritic stainless steel sheet of the present invention is made not to include Nb and Ti, a total of one or both of Al and Si of 5 to 50 at%. This is because if not containing a total of one or both of Al and Si of 5 at% or more, concentration of Al and Si is not sufficient for securing the anti-glare property while obtaining the desired corrosion resistance. On the other hand, even if including one or both of Al and Si in a total of over 50 at%, the effect of improvement of the corrosion resistance becomes saturated.
  • the content of Sn in the surface film is made 1 to 10 at%. This is because if the surface film does not contain Sn, Al and Si cannot be concentrated in the surface film.
  • the high purity ferritic stainless steel sheet of the present invention is made to include at least one of Nb and Ti
  • at least one of Nb and Ti is concentrated at the surface film and can raise the corrosion resistance in the same way as Al and Si.
  • the effect is manifested when the total of the one or more of Ai, Si, Nb, and Ti is contained in the surface film in 5 at% or more. On the other hand, even if exceeding 50 at%, the effect becomes saturated.
  • the average concentration of Cr in the surface film is expressed by the ratio of cations which form the surface film other than the C, O, and N.
  • the contents of Al, Si, Nb, and Ti in the surface film are also expressed by the ratio of cations which form the surface film other than the C, O, and N. The methods of measurement of these will be explained in the following examples, so will be omitted here.
  • Each ferritic stainless steel having a chemical composition of Table 1 was smelted and was hot rolled at an extraction temperature of 1100 to 1200°C to obtain a thickness 3.0 to 6.0 mm hot rolled steel sheet at a coiling temperature of 500 to 700°C.
  • the hot rolled steel sheet was annealed and cold rolled once or twice with process annealing in between so as to produce 0.4 to 0.8 mm thick cold rolled steel sheet.
  • Table 1 (mass%) C Si Mn P S Cr N Al Sn Nb Ti Other elements Remarks A 0.004 0.45 0.08 0.021 0.0005 16.6 0.010 0.45 0.23 - - - Inv.
  • the surface conditions were adjusted by dull roll rolling to surface roughnesses prescribed by the present invention and other roughnesses.
  • the obtained cold rolled steel sheets were all annealed by final annealing at temperatures of 850 to 1000°C where recrystallization ends.
  • the final annealing is performed as annealing in an oxidizing atmosphere or bright annealing.
  • the pickling after the annealing in an oxidizing atmosphere is performed by dipping in an alkali salt bath, neutral salt electrolysis, then dipping in nitric hydrofluoric acid. Steel sheets which were not treated by pickling after bright annealing and further were treated by nitric acid electrolysis were also produced.
  • steel sheets which have surfaces finished by usual cold rolling rolls were also produced as comparative materials. Further, as conventional examples, dull finish steel sheets of SUS304 (18%Cr-8%Ni steel) and SUS444 (22%Cr-1%Mo steel) were prepared.
  • the surface roughness was found by measurement in the rolling direction and the vertical direction to rolling by a 2D roughness meter.
  • the average value of the arithmetic average roughness Ra was given.
  • the surface film was analyzed by nondestructive analysis using X-ray photoelectron spectroscopy.
  • the analysis area was in a range of a vertical 0.1 mm and horizontal 0.1 mm, while the analysis value was the average value of this area.
  • the detection depth was 5 nm or less.
  • the results of analysis were given by the ratios of cations forming the surface film other than C, O, and N.
  • the chemical composition of ingredients of the surface film was given in average values in the surface film.
  • the corrosion resistance was evaluated by the combined cyclic corrosion test based on JASO M609-91.
  • the method of evaluation was made the same as described in the above (b).
  • the degree of corrosion was evaluated based on the conventional examples of SUS304 and SUS444. That is, it was evaluated based on SUS304 where rust spots slightly formed over the entire test surface and SUS444 where almost no rust spots formed. Further, inferior to SUS304 was indicated as "C”, equal to or better than SUS304 was evaluated as "B”, and equal to SUS444 was evaluated as "A".
  • Table 2 shows together the production conditions and the results of evaluation of the different steel sheets.
  • nitric acid% means mass% of concentration of nitric acid in nitric hydrofluoric acid dipping step after alkali salt bath dipping + neutral salt electrolysis.
  • BA indicates bright annealing.
  • H means hydrogen concentration of hydrogen-nitrogen mixed gas
  • DP indicates dew point of gas
  • electrolysis indicates presence of any electrolysis after bright annealing.
  • Nos. 1, 4, 7, 8, 11, 12, 14, and 15 are high purity ferritic stainless steels which have the chemical composition and arithmetic average roughness Ra prescribed in the present invention. These steel sheets were confirmed to have average concentrations of Cr in the surface films prescribed in the present invention. Further, in the surface films, concentration of not only Sn, but also one or more of Al, Si, Ti, and Nb was confirmed. Further, the examples were confirmed to have corrosion resistances equal to or better than SUS304.
  • Nos. 2, 3, 9, 10, 13, and 16 are high purity ferritic stainless steels which satisfy the preferable chemical composition and arithmetic average roughness Ra prescribed in the present invention. These steel sheets were confirmed to have concentrations of Cr in the surface films prescribed in the present invention. Further, in the surface films, confirmation of not only Sn, but also one or more of Al, Si, Ti, and Nb was confirmed. Further, excellent corrosion resistances above SUS304 and equal to SUS444 were confirmed. Note that No. 13 has a content of Cr of 23% or more - which is not preferable from the viewpoint of the alloy costs.
  • Nos. 5 and 6 are examples which have the chemical composition prescribed in the present invention, but have surface roughnesses off from the arithmetic average roughness Ra prescribed in the present invention. These steel sheets did not give the corrosion resistance which is targeted by the present invention.
  • Nos. 17 to 25, 28 and 29 are examples which have the surface roughness prescribed in the present invention, but are off from the chemical composition prescribed in the present invention. These steel sheets did not give the corrosion resistance which is targeted by the present invention.
  • the present invention it is possible to obtain alloy-saving type high purity ferritic stainless steel sheet, without relying on high alloying by addition giving a large content of at least one of Cr and Mo and without limitation to surface film formed by bright annealing, by utilizing the addition of Sn to doubly provide an anti-glare property and corrosion resistance.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Chemical Treatment Of Metals (AREA)
EP12756952.3A 2011-03-14 2012-03-05 High-purity ferritic stainless steel sheet with excellent corrosion resistance and anti-glare properties Active EP2687617B1 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2011055947A JP5709594B2 (ja) 2011-03-14 2011-03-14 耐銹性と防眩性に優れた高純度フェライト系ステンレス鋼板
PCT/JP2012/055583 WO2012124528A1 (ja) 2011-03-14 2012-03-05 耐銹性と防眩性に優れた高純度フェライト系ステンレス鋼板

Publications (3)

Publication Number Publication Date
EP2687617A1 EP2687617A1 (en) 2014-01-22
EP2687617A4 EP2687617A4 (en) 2014-10-15
EP2687617B1 true EP2687617B1 (en) 2020-05-20

Family

ID=46830603

Family Applications (1)

Application Number Title Priority Date Filing Date
EP12756952.3A Active EP2687617B1 (en) 2011-03-14 2012-03-05 High-purity ferritic stainless steel sheet with excellent corrosion resistance and anti-glare properties

Country Status (9)

Country Link
US (1) US9289964B2 (pt)
EP (1) EP2687617B1 (pt)
JP (1) JP5709594B2 (pt)
KR (3) KR20150119500A (pt)
CN (2) CN106978569A (pt)
BR (1) BR112013023476B1 (pt)
ES (1) ES2802677T3 (pt)
TW (1) TWI465585B (pt)
WO (1) WO2012124528A1 (pt)

Families Citing this family (21)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103608479B (zh) 2011-06-16 2016-09-07 新日铁住金不锈钢株式会社 抗皱性优良的铁素体系不锈钢板及其制造方法
TWI504763B (zh) * 2012-10-30 2015-10-21 Nippon Steel & Sumikin Sst High-heat-resistant fat iron-based stainless steel plate
WO2014142302A1 (ja) * 2013-03-14 2014-09-18 新日鐵住金ステンレス株式会社 時効熱処理後の強度増加が小さいフェライト系ステンレス鋼板及びその製造方法
KR101712333B1 (ko) * 2013-03-25 2017-03-03 닛폰 스틸 앤드 스미킨 스테인레스 스틸 코포레이션 펀칭 가공성이 우수한 페라이트계 스테인리스 강판 및 그 제조 방법
CN105074035B (zh) * 2013-03-27 2018-02-16 新日铁住金不锈钢株式会社 研磨后的表面耐蚀性优异的铁素体系不锈钢及其制造方法
JP6067134B2 (ja) * 2013-11-01 2017-02-01 新日鐵住金ステンレス株式会社 燃料改質器用フェライト系ステンレス鋼およびその製造方法
CN106460112A (zh) * 2014-05-14 2017-02-22 杰富意钢铁株式会社 铁素体系不锈钢
EP3118342B1 (en) * 2014-05-14 2018-12-26 JFE Steel Corporation Ferritic stainless steel
JP6159775B2 (ja) * 2014-10-31 2017-07-05 新日鐵住金ステンレス株式会社 耐排ガス凝縮水腐食性とろう付け性に優れたフェライト系ステンレス鋼及びその製造方法
ES2922207T3 (es) * 2014-10-31 2022-09-09 Nippon Steel Stainless Steel Corp Acero inoxidable a base de ferrita con alta resistencia a la corrosión provocada por gases de escape y condensación y altas propiedades de soldadura fuerte y método de fabricación del mismo
EP3095882B1 (en) * 2015-05-18 2021-09-22 Outokumpu Oyj Method for producing a stainless steel sheet with modified visual characteristics
JP7058537B2 (ja) * 2018-03-30 2022-04-22 日鉄ステンレス株式会社 耐塩害腐食性に優れたフェライト系ステンレス鋼
JP6722740B2 (ja) * 2018-10-16 2020-07-15 日鉄ステンレス株式会社 磁気特性に優れたフェライト系ステンレス鋼
CN109182912A (zh) * 2018-10-24 2019-01-11 东北大学 一种稀土处理含铜锡430铁素体不锈钢及其制备方法
KR102146317B1 (ko) * 2018-11-29 2020-08-20 주식회사 포스코 내식성이 향상된 페라이트계 스테인리스강 및 그 제조 방법
JP7186601B2 (ja) * 2018-12-21 2022-12-09 日鉄ステンレス株式会社 高圧水素ガス用機器の金属材料として用いるＣｒ系ステンレス鋼
KR20220017884A (ko) * 2019-06-11 2022-02-14 미쯔비시 가스 케미칼 컴파니, 인코포레이티드 수성 조성물, 이것을 이용한 스테인리스강 표면의 조화처리방법, 그리고 조화처리된 스테인리스강 및 그의 제조방법
CN111276311B (zh) * 2020-02-18 2021-07-09 北京科技大学 一种Fe-B-P-C-Cu-N-Cr系非晶纳米晶软磁合金及制备方法
JP7482666B2 (ja) * 2020-03-30 2024-05-14 日鉄ステンレス株式会社 フェライト系ステンレス鋼およびフェライト系ステンレス鋼の製造方法
CN114901848B (zh) * 2020-05-28 2023-09-19 日铁不锈钢株式会社 铁素体系不锈钢钢材及耐蚀性构件
CN115261744B (zh) * 2022-07-20 2023-10-27 山西太钢不锈钢股份有限公司 一种高韧性低铬铁素体不锈钢中厚板及其制造方法

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2954003B2 (ja) * 1995-09-28 1999-09-27 川崎製鉄株式会社 ダル仕上ステンレス鋼板の製造方法
JP3224694B2 (ja) * 1994-10-07 2001-11-05 新日本製鐵株式会社 耐銹性と加工性に優れたフェライト系ステンレス鋼板
JP2003094255A (ja) * 2001-09-27 2003-04-03 Nippon Steel Corp 圧延用ロールの放電加工方法

Family Cites Families (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2826225B2 (ja) 1991-12-13 1998-11-18 川崎製鉄株式会社 防眩性と耐食性を兼ね備えた外装用ステンレス鋼板
JP2689377B2 (ja) 1992-12-17 1997-12-10 川崎製鉄株式会社 防眩性、色調均一性及び耐食性に優れたダル仕上ステンレス鋼板の製造方法
JP3401350B2 (ja) 1994-12-14 2003-04-28 日新製鋼株式会社 色調安定性，防眩性及び耐食性に優れたフェライト系ステンレス鋼板及びその製造方法
JP2974597B2 (ja) 1995-09-28 1999-11-10 川崎製鉄株式会社 ダル仕上ステンレス鋼板の製造方法
JP3499361B2 (ja) * 1996-02-26 2004-02-23 新日本製鐵株式会社 防眩性と耐食性を兼ね備えたステンレス鋼板
JP4070253B2 (ja) 1996-04-24 2008-04-02 新日鐵住金ステンレス株式会社 防眩性に優れた高耐銹フェライト系ステンレス鋼板およびその製造方法
JPH1112704A (ja) * 1997-06-30 1999-01-19 Kawasaki Steel Corp 大気中での耐銹性に優れるフェライト系ステンレス鋼およびその製造方法
JP3901295B2 (ja) 1997-08-11 2007-04-04 日新製鋼株式会社 高Ｃｒ含有光輝焼鈍ステンレス鋼の水素脆性を除去する熱処理方法ならびに加工性の良い建材用ステンレス鋼板およびその製造方法
JP4226131B2 (ja) 1999-02-16 2009-02-18 新日鐵住金ステンレス株式会社 耐汚染性、洗浄性、防眩性に優れたステンレス鋼帯の製造方法
JP4906193B2 (ja) * 2000-04-13 2012-03-28 新日鐵住金ステンレス株式会社 フェライト系快削ステンレス鋼
JP4651682B2 (ja) 2008-01-28 2011-03-16 新日鐵住金ステンレス株式会社 耐食性と加工性に優れた高純度フェライト系ステンレス鋼およびその製造方法
JP5320034B2 (ja) * 2008-11-14 2013-10-23 新日鐵住金ステンレス株式会社 加熱後耐食性に優れた自動車排気系部材用省Ｍｏ型フェライト系ステンレス鋼
JP4624473B2 (ja) 2008-12-09 2011-02-02 新日鐵住金ステンレス株式会社 耐銹性に優れた高純度フェライト系ステンレス鋼およびその製造方法

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3224694B2 (ja) * 1994-10-07 2001-11-05 新日本製鐵株式会社 耐銹性と加工性に優れたフェライト系ステンレス鋼板
JP2954003B2 (ja) * 1995-09-28 1999-09-27 川崎製鉄株式会社 ダル仕上ステンレス鋼板の製造方法
JP2003094255A (ja) * 2001-09-27 2003-04-03 Nippon Steel Corp 圧延用ロールの放電加工方法

Also Published As

Publication number Publication date
TW201245467A (en) 2012-11-16
CN103429777A (zh) 2013-12-04
KR20130123433A (ko) 2013-11-12
BR112013023476A2 (pt) 2016-12-06
US9289964B2 (en) 2016-03-22
KR102046742B1 (ko) 2019-11-19
US20130337289A1 (en) 2013-12-19
WO2012124528A1 (ja) 2012-09-20
CN106978569A (zh) 2017-07-25
TWI465585B (zh) 2014-12-21
EP2687617A1 (en) 2014-01-22
EP2687617A4 (en) 2014-10-15
KR20180133567A (ko) 2018-12-14
KR20150119500A (ko) 2015-10-23
JP2012193392A (ja) 2012-10-11
JP5709594B2 (ja) 2015-04-30
ES2802677T3 (es) 2021-01-20
BR112013023476A8 (pt) 2018-04-17
BR112013023476B1 (pt) 2018-11-27

Similar Documents

Publication Publication Date Title
EP2687617B1 (en) High-purity ferritic stainless steel sheet with excellent corrosion resistance and anti-glare properties
EP2554701B1 (en) Ferritic stainless steel sheet superior in surface glossiness and corrosion resistance and method for producing same
US8721960B2 (en) High-purity ferritic stainless steels excellent in corrosion resistance and method of production of same
EP2677055B1 (en) High-purity ferritic stainless steel sheet having excellent oxidation resistance and high-temperature strength, and method for producing same
EP3438310B1 (en) Ferritic stainless steel sheet used for tig welding
EP3098330B1 (en) Material for cold-rolled stainless steel sheet and method for producing same
TWI516614B (zh) Fat iron stainless steel
EP3231882B1 (en) Stainless steel and production method therefor
WO2016051437A1 (ja) フェライト系ステンレス鋼およびその製造方法
JP5862846B2 (ja) フェライト系ステンレス鋼およびその製造方法
JP6411881B2 (ja) フェライト系ステンレス鋼およびその製造方法
JP5556951B2 (ja) フェライト系ステンレス鋼
WO2022168167A1 (ja) 薄鋼板
CN112795831A (zh) 铁素体系不锈钢板的制造方法

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 20131004

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

DAX Request for extension of the european patent (deleted)
A4 Supplementary search report drawn up and despatched

Effective date: 20140915

RIC1 Information provided on ipc code assigned before grant

Ipc: B32B 15/01 20060101ALI20140909BHEP

Ipc: C22C 38/06 20060101ALI20140909BHEP

Ipc: C22C 38/02 20060101ALI20140909BHEP

Ipc: C22C 38/00 20060101AFI20140909BHEP

Ipc: C22C 38/26 20060101ALI20140909BHEP

Ipc: C22C 38/28 20060101ALI20140909BHEP

Ipc: C21D 8/02 20060101ALI20140909BHEP

Ipc: C22C 38/54 20060101ALI20140909BHEP

Ipc: C22C 38/32 20060101ALI20140909BHEP

Ipc: C21D 6/00 20060101ALI20140909BHEP

Ipc: C22C 38/04 20060101ALI20140909BHEP

Ipc: C22C 38/18 20060101ALI20140909BHEP

17Q First examination report despatched

Effective date: 20160905

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: EXAMINATION IS IN PROGRESS

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: GRANT OF PATENT IS INTENDED

INTG Intention to grant announced

Effective date: 20190703

GRAJ Information related to disapproval of communication of intention to grant by the applicant or resumption of examination proceedings by the epo deleted

Free format text: ORIGINAL CODE: EPIDOSDIGR1

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: EXAMINATION IS IN PROGRESS

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: GRANT OF PATENT IS INTENDED

INTC Intention to grant announced (deleted)
INTG Intention to grant announced

Effective date: 20191205

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE PATENT HAS BEEN GRANTED

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: FI

Ref legal event code: FGE

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602012070223

Country of ref document: DE

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 1272647

Country of ref document: AT

Kind code of ref document: T

Effective date: 20200615

REG Reference to a national code

Ref country code: SE

Ref legal event code: TRGR

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20200520

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200921

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200920

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200820

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200821

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200520

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200820

Ref country code: RS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200520

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200520

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200520

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 1272647

Country of ref document: AT

Kind code of ref document: T

Effective date: 20200520

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200520

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200520

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2802677

Country of ref document: ES

Kind code of ref document: T3

Effective date: 20210120

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200520

Ref country code: AT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200520

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200520

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200520

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200520

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200520

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602012070223

Country of ref document: DE

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200520

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200520

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

26N No opposition filed

Effective date: 20210223

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200520

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200520

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20210305

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20210331

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210305

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210305

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210331

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210331

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210305

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210331

REG Reference to a national code

Ref country code: DE

Ref legal event code: R081

Ref document number: 602012070223

Country of ref document: DE

Owner name: NIPPON STEEL STAINLESS STEEL CORPORATION, JP

Free format text: FORMER OWNER: NIPPON STEEL & SUMIKIN STAINLESS STEEL CORPORATION, TOKYO, JP

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO

Effective date: 20120305

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200520

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200520

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FI

Payment date: 20240319

Year of fee payment: 13

Ref country code: DE

Payment date: 20240325

Year of fee payment: 13

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: SE

Payment date: 20240319

Year of fee payment: 13

Ref country code: IT

Payment date: 20240308

Year of fee payment: 13

Ref country code: FR

Payment date: 20240129

Year of fee payment: 13

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200520

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: ES

Payment date: 20240402

Year of fee payment: 13

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200520